Semiconductor having low concentration of phosphorous

ABSTRACT

A non-single-crystalline semiconductor material and a device utilizing the material, the material being of an intrinsic or substantially intrinsic conductivity type and including silicon and containing a dangling bond neutralizer consisting of hydrogen and/or a halogven wherein the concentration of carbon contained in the semiconductor material is less than 4x1018 and the concentration of boron contained in the semiconductor material is not higher than 2x1017 atoms/cm3.

This is a Divisional application of Ser. No. 08/350,169, filed Nov. 30, 1994; now abandoned which itself is a continuation of Ser. No. 07/748,421, filed Aug. 22, 1991; now abandoned which itself was a divisional of Ser. No. 07/443,015, filed Nov. 29, 1989, now U.S. Pat. No. 5,077,223; which was a continuation of Ser. No. 06/785,586, filed Oct. 8, 1985; now abandoned which was a divisional of Ser. No. 06/564,213, filed Dec. 22, 1983, now U.S. Pat. No. 4,581,476, which in turn, was a continuation-in-part of Ser. No. 06/525,459 filed Aug. 22, 1983, now U.S. Pat. No. 4,591,892.

BACKGROUND OF THE INVENTION

1. Field of the Invention

The present invention relates to a photoelectric conversion device which has a non-single-crystal semiconductor laminate member having formed therein at least one PIN junction, and a method for the manufacture of such a photoelectric conversion device.

2. Description of the Prior Art

A photoelectric conversion device of the type including a non-single-crystal semiconductor laminate member having formed therein at least one PIN junction usually has the non-single-crystal semiconductor laminate member formed on a substrate having a conductive surface and a conductive layer formed on the non-single-crystal semiconductor laminate member. The non-single-crystal semiconductor laminate member has at least a first non-single-crystal semiconductor layer of a P or N first conductivity type, an I type second non-single-crystal semiconductor layer formed on the first non-single-crystal semiconductor layer, and a third non-single-crystal semiconductor layer formed on the second non-single-crystal semiconductor layer and having a second conductivity type opposite from the first conductivity type. The first, second, and third non-single-crystal semiconductor layers form one PIN junction.

In this case, for example, the substrate has such a structure that a light-transparent conductive layer is formed as a first conductive layer on a light-transparent insulating substrate body. The first and third non-single-crystal semiconductor layers of the non-single-crystal semiconductor laminate member are P- and N-type, respectively. Further, the conductive layer on the non-single-crystal semiconductor laminate member is formed as a second conductive layer on the N-type third non-single-crystal semiconductor layer.

With the photoelectric conversion device of such a structure as described above, when light is incident on the side of the light-transparent substrate towards the non-single-crystal semiconductor laminate member, electron-hole pairs are created by the light in the I-type second non-single-crystal semiconductor layer. Holes of the electron-hole pairs thus created pass through the P-type first non-single-crystal semiconductor layer to reach the first conductive layer, and electrons flow through the N-type third non-single-crystal semiconductor layer into the second conductive layer. Therefore, photocurrent is supplied to a load which is connected between the first and second conductive layers, thus providing a photoelectric conversion function.

In conventional photoelectric conversion devices of the type described above, however, since the I-type second non-single-crystal semiconductor layer is formed to contain oxygen with a concentration above 10²⁰ atoms/cm³, and/or carbon with a concentration above 10²⁰ atoms/cm³, and/or phosphorus with a concentration as high as above 5×10¹⁷ atoms/cm³, the I-type non-single-crystal semiconductor layer inevitably contains impurities imparting N conductivity type, with far lower concentrations than in the P-type first non-single-crystal semiconductor layer and the N-type third non-single-crystal semiconductor layer.

In addition, the impurity concentration has such a distribution that it undergoes substantially no variations in the thickness direction of the layer.

On account of this, in the case where the second non-single-crystal semiconductor layer is formed thick with a view to creating therein a large quantity of electron-hole pairs in response to the incidence of light, a depletion layer, which spreads into the second non-single-crystal semiconductor layer from the PI junction defined between the P-type first and the I-type second non-single-crystal semiconductor layers, and a depletion layer, which spreads into the second non-single-crystal semiconductor layer from the NI junction defined between the N-type third and the I-type second non-single-crystal semiconductor layers, are not linked together. In consequence, the second non-single-crystal semiconductor layer has, over a relatively wide range thickness thereof at the central region in that direction, a region in which the bottom of the conduction band and the top of the valence band of its energy band are not inclined in the directions necessary for the holes and electrons to drift towards the first and third non-single-crystal semiconductor layers, respectively. Therefore, the holes and electrons of the electron-hole pairs created by the incident light in the second non-single-crystal semiconductor layer, in particular, the electrons and holes generated in the central region of the second layer in its thickness direction, are not effectively directed to the first and third non-single-crystal semiconductor layers, respectively.

Accordingly, the prior art photoelectric conversion devices of the above-described structure have the defect that even if the second non-single-crystal semiconductor layer is formed thick for creating a large quantity of electron-hole pairs in response to incident light, a high photoelectric conversion efficiency cannot be obtained.

Further, even if the I-type second non-single-crystal semiconductor layer is thick enough to permit the depletion layer extending into the second non-single-crystal semiconductor layer from the PI junction between the P-type first non-single-crystal semiconductor layer on the side on which light is incident and the I-type second non-single-crystal semiconductor layer formed on the first semiconductor layer and the depletion layer extending into the second non-single-crystal semiconductor layer from the NI junction between the N-type third non-single-crystal semiconductor layer on the side opposite from the side of the incidence of light and the I-type second non-single-crystal semiconductor layer are linked together, the expansion of the former depletion layer diminishes with the lapse of time for light irradiation by virtue of a known light irradiation effect commonly referred to as the Staebler-Wronski effect, because the I-type non-single-crystal semiconductor layer forming the PI junction contains impurities which impart N conductivity type as mentioned previously. Finally, the above-said depletion layers are disconnected from each other. In consequence, there is formed in the central region of the second non-single-crystal semiconductor layer in the thickness direction thereof a region in which the bottom of the conduction band and the top of the valence band of the energy band are not inclined in the directions in which the holes and electrons of the electron-hole pairs created by the incidence of light are drifted towards the first and third non-single-crystal semiconductor layers, respectively.

Accordingly, the conventional photoelectric conversion devices of the above-said construction have the defect that the photoelectric conversion efficiency is impaired by the long-term use of the devices.

SUMMARY OF THE INVENTION

It is therefore an object of the present invention to provide a novel photoelectric conversion device which is able to achieve a far higher photoelectric conversion efficiency than that obtainable with the conventional devices described above.

Another object of the present invention is to provide a novel photoelectric conversion device the photoelectric conversion efficiency of which is hardly or only slightly lowered by the Staebler-Wronski effect even if it is used for a long period of time.

Yet another object of the present invention is to provide a novel method which permits easy manufacture of the photoelectric conversion device having the above-said excellent features.

In accordance with an aspect of the present invention, the first (or third) non-single-crystal semiconductor layer of the non-single-crystal laminate member is a layer on the side on which light is incident and is of P conductivity type, and the I-type second non-single-crystal semiconductor layer has introduced therein an impurity for imparting thereto type P conductivity, which is distributed so that the impurity concentration continuously decreases towards the third (or first) non-single-crystal semiconductor layer in the thickness direction of the I-type layer.

In this case, for example, the substrate is light-transparent and, accordingly, the first non-single-crystal semiconductor layer is disposed on the side where light is incident. The first and third non-single-crystal semiconductor layers are P- and N-type, respectively, and the I-type second non-single-crystal semiconductor layer has introduced therein an impurity for imparting thereto P-type conductivity, such as boron, so that its concentration in the region adjacent the first non-single-crystal semiconductor layer is higher than the concentration in the region adjacent the third non-single-crystal semiconductor layer.

On account of this, even if the I-type second non-single-crystal semiconductor layer is formed relatively thick for creating therein a large quantity of electron-hole pairs in response to the incidence of light, the depletion layer extending into the second non-single-crystal semiconductor layer from the PI junction between the first and second non-single-crystal semiconductor layers and the depletion layer extending into the second non-single-crystal layer from the NI junction between the third and second non-single-crystal semiconductor layers are joined together. Accordingly, the holes and electrons which are produced in the central region of the second non-single-crystal semiconductor layer in its thickwise direction are also effectively drifted towards the first and third non-single-crystal semiconductor layers, respectively.

Moreover, even if the I-type second non-single-crystal semiconductor layer contains impurities which impart N-type conductivity thereto, because it is formed to contain oxygen and/or carbon and phosphorus in large quantities as described previously, boron, which imparts P-type conductivity and is introduced into the second non-single-crystal semiconductor layer, combines with oxygen, and/or carbon, and/or phosphorus. Besides, the P-type impurity introduced into the second non-single-crystal semiconductor layer has a high concentration in the region thereof adjacent the P-type first non-single-crystal semiconductor layer, that is, on the side of the PI junction. Therefore, the expansion of the depletion layer spreading into the second non-single-crystal semiconductor layer from the PI junction between the first and second non-single-crystal semiconductor layers is scarcely or only slightly diminished by the light irradiation effect (the Staebler-Wronski effect).

Accordingly, the photoelectric conversion device of the present invention retains a high photoelectric conversion efficiency, even if used for a long period of time.

In accordance with another aspect of the present invention, the second non-single-crystal semiconductor layer, which has introduced thereinto an impurity which imparts P-type conductivity, with such a distribution that its concentration continuously decreases towards the N-type third (or first) non-single-crystal semiconductor layer in the thickness direction of the second layer, can easily be formed, through a CVD (Chemical Vapor Deposition) method using a semiconductor material gas and an impurity material gas for imparting P-type conductivity, merely by continuously decreasing (or increasing) the concentration of the depart material gas relative to the semiconductor material gas with the lapse of time.

Accordingly, the manufacturing method of the present invention allows easy fabrication of the photoelectric conversion device of the present invention which possesses the aforementioned advantages.

Other objects, features and advantages of the present invention will become more fully apparent from the detailed description taken in conjunction with the accompanying drawings.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. IA to D are sectional views schematically illustrating a sequence of steps involved in the manufacture of a photoelectric conversion device in accordance with an embodiment of the present invention;

FIG. 2A is a sectional view schematically illustrating a first embodiment of the photoelectric conversion device by the manufacturing method shown in FIG. 1;

FIG. 2B is a graph showing the concentration distributions of impurities introduced into first, second, and third non-single-crystal semiconductor layers of the photoelectric conversion device depicted in FIG. 2A;

FIG. 2C is a graph showing the energy band of the photoelectric conversion device shown in FIG. 2A;

FIG. 3 is a graph showing the voltage V (volt)- current density I (mA/cm²) characteristic of the photoelectric conversion device of FIG. 2, in comparison with the characteristic of a conventional photoelectric conversion device;

FIG. 4 is a graph showing variations (%) in the photoelectric conversion efficiency of the photoelectric conversion device of the present invention, shown in FIG. 2, in comparison with a conventional photoelectric conversion device;

FIG. 5A is a sectional view schematically illustrating a second embodiment of the photoelectric conversion device of the present invention;

FIG. 5B is a graph showing concentration distributions of impurities introduced into first, second, and third non-single-crystal semiconductor layers of the second embodiment of the present invention;

FIG. 6A is a sectional view schematically illustrating a third embodiment of the photoelectric conversion device of the present invention; and

FIG. 6B is a graph showing the concentration distributions of impurities introduced into first, second, and third non-single-crystal semiconductor layers of the photoelectric conversion device shown in FIG. 6A.

DESCRIPTION OF THE PREFERRED EMBODIMENTS

A description will be given of, with reference to FIGS. 1 and 2, of a first embodiment of the photoelectric conversion device of the present invention, along with the manufacturing method of the present invention.

The manufacture of the photoelectric conversion device starts with the preparation of an insulating, light-transparent substrate 1 as of glass (FIG. 1).

A light-transparent conductive layer 2 is formed on the substrate 1 (FIG. 1B).

The conductive layer 2 is formed of, for example, a tin oxide, or a light-transparent conductive material consisting principally of a tin oxide. The conductive layer 2 is formed by, for example, a known vacuum evaporation method to a thickness of, for instance, 0.1 to 0.2 μm.

Next, a non-single-crystal semiconductor laminate member 3 is formed on the conductive layer 2 (FIG. 1C).

The non-single-crystal semiconductor laminate member 3 has such a structure that a P-type non-single-crystal semiconductor layer 4, an I-type non-single-crystal semiconductor layer 5 and an N-type non-single-crystal semiconductor layer 6 are sequentially formed in this order. These non-single-crystal semiconductor layers 4, 5 and 6 form PIN junction.

The non-single-crystal semiconductor layer 4 of the non-single-crystal semiconductor laminate member 3 is formed of, for example, Si, Si_(x)C_(1-x) (where 0<×<1, for instance, x=0.8) or Ge in an amorphous, semi-amorphous, or microcrystalline form. The non-single-crystal semiconductor layer 4 is, for example, 100 angstroms thick.

The non-single-crystal semiconductor layer 4 is formed by a CVD method which employs a semiconductor material gas composed of a hydride or halide of a semiconductor, such as Si, Si_(x) C_(1-x) (where 0<×<1), or Ge, and an impurity material gas composed of a hydride or halide of a P-type impurity, for instance, diborane (B₂H₆). The CVD method may or may not employ a glow discharge (plasma), or light. In this case, the non-single-crystal semiconductor layer 4 has a P-type impurity introduced therein (boron) in a concentration as high as 1×10¹⁹ to 6×10²⁰ atoms/cm³, as shown in FIG. 2B.

The non-single-crystal semiconductor layer 5 is formed of, for instance, amorphous or semi-amorphous silicon, and has a thickness of, for example, 0.3 to 0.8 μm, in particular, 0.5 μm.

The non-single-crystal semiconductor layer 5 is formed by a CVD method which uses a semiconductor raw material gas composed of a hydride or halide of silicon, for example, Si_(n)H_(2n+2) (where n is greater than or equal to 1), or SiF_(m) (where m is greater than or equal to 2), and a deposit impurity material gas composed of a hydride or halide of a P-type impurity, for instance, diborane (B₂H₆), the CVD method may employ or may not employ a glow discharge (plasma), or light. In this case, by decreasing the concentration of the deposit material gas relative to the concentration of the semiconductor raw material gas within a range of less than 5 ppm with the lapse of time, the non-single-crystal semiconductor layer 5 is formed having introduced thereinto a P-type impurity (boron), the concentration of which linearly and continuously decreases in the thickness direction of the layer towards the non-single-crystal semiconductor layer 6 as shown in FIG. 2B. The concentration of the P-type impurity in the non-single-crystal semiconductor layer 5 is high on the side of the non-single-crystal semiconductor layer 4 as compared with the impurity concentration on the side of the non-single-crystal semiconductor layer 6. The ratio of the impurity concentration in the layer 5 at one end thereof adjacent the layer 6 to the concentration at the other end adjacent the layer 4 is {fraction (1/10)} to {fraction (1/100)}, preferably, {fraction (1/20)} to {fraction (1/40)}. In practice, the P-type impurity (boron) has a concentration of 2×10¹⁵ to 2×10¹⁷ atoms/cm³ at the end of the layer 5 adjacent the layer 4 and a concentration below 1×10¹⁵ atoms/cm³ at the end of the layer 5 adjacent the layer 6.

The non-single-crystal semiconductor layer 5 is formed by the above-said CVD method. In this case, the semiconductor raw material gas is one that is obtained by passing a semiconductor raw material gas through a molecular sieve or zeolite which adsorbs oxygen, and/or carbon and/or phosphorus. Accordingly, the non-single-crystal semiconductor layer 5 is formed to contain oxygen at a concentration less than 5×10¹⁹ and as low as 5×10¹⁸ atoms/cm³, and/or carbon at a concentration less than 4×10¹⁸ and as low as 4×10¹⁵ atoms/cm³, and/or phosphorus at a concentration at least as low as 5×10¹⁵ atoms/cm³.

The non-single-crystal semiconductor layer 6 is formed of, for instance, microcrystalline silicon, and has a thickness of, for example, 100 to 300 angstroms.

The non-single-crystal semiconductor layer 6 is formed by a CVD method which employs a semiconductor raw material gas composed of a hydride or halide of silicon, for example, Si_(n)H_(2n+2) (where n is greater than or equal to 1) or SiF_(m) (where m is greater than or equal to 2), and an impurity material gas composed of a hydride or halide of an N-type impurity, for instance, phosphine (PH₃). The CVD method may or may not employ a glow discharge (plasma) light. In this case, the non-single-crystal semiconductor layer 6 has an N-type impurity (phosphorus) introduced thereinto with a concentration of 1×10¹⁹ to 6×10²⁰ atoms/cm³, as shown in FIG. 2.

Next, a conductive layer 7 is formed on the non- single-crystal semiconductor laminate member 3 made up of the non-single-crystal semiconductor layers 4, 5 and 6, that is, on the non-single-crystal semiconductor layer 6 (FIG. 1D).

The conductive layer 7 has such a structure that a light-transparent conductive layer 8 formed of, for example, a tin oxide or a light-transparent conductive material consisting principally of tin oxide, and a reflective conductive layer 9 formed of a metal, such as aluminum, silver, or the like, are formed in this order. In this case, the conductive layer 8 is formed to a thickness of 900 to 1300 angstroms thick by means of, for example, vacuum evaporation, and the conductive layer 9 is also formed by vacuum evaporation.

In the manner described above, the first embodiment of the photoelectric conversion device of the present invention shown in FIG. 2A is manufactured.

With the photoelectric conversion device shown in FIG. 2A, when light 10 is incident on the side of the substrate 1 towards the non-single-crystal semiconductor laminate member 3, electron-hole pairs are created in the I-type non-single-crystal semiconductor layer 5 in response to the light 10. The holes of the electron-hole pairs thus produced flow through the P-type non-single-crystal semiconductor layer 4 into the light-transparent conductive layer 2, and the electrons flow through the N-type non-single-crystal semiconductor layer 6 into the conductive layer 7. Therefore, photocurrent is supplied to a load which is connected between the conductive layers 2 and 7, thus providing the photoelectric conversion function.

In this case, the I-type non-single-crystal semiconductor layer 5 has a P-type impurity (boron) introduced thereinto which is distributed so that the impurity concentration continuously decreases towards the non-single-crystal semiconductor layer 6 in the thickness direction of the layer 5, as shown in FIG. 2B. On account of this, even if the I-type non-single-crystal semiconductor layer 5 is formed thick for generating therein a large quantity of electron-hole pairs in response to the incidence of light, a depletion layer (not shown) which extends into the non-single-crystal semiconductor layer 5 from the PI junction 11 between the P-type non-single-crystal semiconductor layer 4 and the I-type non-single-crystal semiconductor layer 5 and a depletion (not shown) layer which extends into the non-single-crystal semiconductor layer 5 from the NI junction 12 between the N-type non-single-crystal semiconductor layer 6 and the non-single-crystal semiconductor layer 5 are joined together. Therefore, the I-type non-single-crystal semiconductor layer 5, as viewed from the bottom of the conduction band and the top of the valence bands of its energy band, has a gradient that effectively causes holes and electrons to drift towards the non-single-crystal semiconductor layers 4 and 6, respectively.

Accordingly, the photoelectric conversion device of the present invention, shown in FIG. 2A, achieves a higher photoelectric conversion efficiency than the conventional photoelectric conversion devices.

By the way, according to a photoelectric conversion device corresponding to the conventional one and which is identical in construction with the photoelectric conversion device of the present invention shown in FIG. 2A, except that the concentration of the N-type impurity in the I-type non-single-crystal semiconductor layer 5 is about 10¹⁶ atoms/cm³ which is far lower than the impurity concentrations in the P-type and N-type non-single-crystal semiconductor layers 4 and 6 because the I-type non-single-crystal semiconductor layer 5 is formed to contain oxygen, and/or carbon, and/or phosphorus in large quantities, as referred to previously, provided a voltage V (volt)-current density I (mA/cm²) characteristic as indicated by a curve 30 in FIG. 3. Accordingly, the open-circuit voltage was 0.89 V, the short-circuit current density I was 16.0 mA/cm², the fill factor was 61%, and the photoelectric conversion efficiency about 8.7%. In contrast thereto, the photoelectric conversion device of the present invention shown in FIG. 2A, provided the voltage V -current density I characteristic as indicated by curve 31 in FIG. 3. Accordingly, the open-circuit voltage V was 0.92 V, which is higher than was obtained with the above-said device corresponding to the prior art device; the current density I was 19.5 mA/cm²; the fill factor was 68%; and the photoelectric conversion efficiency was about 12.2%. Incidentally, these results were obtained under the conditions wherein a photoelectric conversion devices, each having the non-single-crystal semiconductor laminate member 3 of a 1.05 cm² area, were exposed to irradiation by light with an intensity of AM1 (100 mW/cm²).

In the case of the photoelectric conversion device of the present invention shown in FIG. 2A, since the I-type non-single-crystal semiconductor layer 5 has boron introduced thereinto as a P-type impurity the boron combines with the oxygen and/or carbon and/or phosphorus contained in the non-single-crystal semiconductor layer 5. In addition, the concentration of the P-type impurity (boron) is high on the side of the PI junction 11, that is, on the side of the P-type non-single-crystal semiconductor layer 4. Accordingly, the expansion of the depletion layer extending into the I-type non-single-crystal semiconductor layer 5 from the PI junction 11 between the P-type non-single-crystal semiconductor layer 4 and the I-type non-single-crystal semiconductor layer 5 is hardly or only slightly diminished by the light irradiation effect (the Staebler-Wronski effect).

For this reason, according to the photoelectric conversion device of the present invention, the aforesaid high photoelectric conversion efficiency is hardly impaired by long-term use.

In addition, the aforesaid photoelectric conversion device corresponding to the prior art one which provided the voltage V-current density I characteristic indicated by the curve 30 in FIG. 3 exhibited, variations (%) in the photoelectric conversion efficiency relative to the light irradiation time T (hr) as indicated by curve 40 in FIG. 4. In contrast thereto, in the case of the photoelectric conversion device of the present invention, the photoelectric conversion efficiency varied with the light irradiation time T as indicated by curve 41 in FIG. 4. That is, the photoelectric conversion efficiency slightly increased in an early stage and, thereafter, it decreased only very slightly with time. These result were also obtained under the same conditions mentioned previously in connection with FIG. 3.

As described above, the first embodiment of the photoelectric conversion device of the present invention possesses the advantage that it provides a high photoelectric conversion efficiency than the conventional photoelectric conversion devices, even when used for a long period of time.

Further, the manufacturing method of the present invention shown in FIG. 1 employs a series of simple steps such as forming the conductive layer 2 on the substrate 1, forming the non-single-crystal semiconductor layers 4, 5 and 6 on the conductive layer 2 through the CVD method to provide the non-single-crystal semiconductor laminate member 3 and forming a conductor layer 7 on the non-single-crystal semiconductor laminate member 3. The I-type non-single-crystal semiconductor layer 5 is formed by the CVD method using a semiconductor raw material gas and a P-type deposit (boron) gas and, in this case, simply by continuously changing the concentration of the deposit material gas relative to the concentration of the semiconductor raw material gas as a function of time, the P-type impurity is introduced into the layer 5 with such a concentration distribution that its concentration continuously decreases towards the non-single-crystal semiconductor layer 6 in the thickness direction of the layer 5.

Accordingly, the manufacturing method of the present invention allows ease in the fabrication of the photoelectric conversion device of the present invention which has the aforementioned advantages.

Incidentally, the first embodiment illustrated in FIG. 2 shows the case in which the impurity contained in the I-type non-single-crystal semiconductor layer 5 has such a concentration distribution as shown in FIG. 2B in which the concentration linearly and continuously drops towards the non-single-crystal semiconductor layer 6.

As will be appreciated from the above, however, even if the impurity introduced in the I-type non-single-crystal semiconductor layer 5 has a concentration profile such that the impurity concentration drops stepwise and continuously towards the non-single-crystal semiconductor layer 6 as shown in FIG. 5B which illustrates a second embodiment of the present invention, and even if the impurity in the layer 5 has such a concentration distribution that the impurity concentration decreases non-linearly and continuously towards the layer 6 in a manner to obtain a concentration distribution such that the impurity concentration abruptly drops in the end portion of the layer 5 adjacent the layer 6 as shown in FIG. 6 which illustrates a third embodiment of the present invention, the photoelectric conversion device of the present invention produces the same excellent operation and effects as are obtainable with the photoelectric conversion device shown in FIG. 2.

Further, the foregoing description has been given of the case where light is incident on the photoelectric conversion device from the side of the substrate 1 and, accordingly, the non-single-crystal semiconductor layer 4 of the non-single-crystal semiconductor laminate member 3 on the side on which the light is incident is P-type.

But, also in case where the photoelectric conversion device is arranged to be exposed to light on the side opposite from the substrate 1, the non-single-crystal semiconductor layer 6 of the non-single-crystal semiconductor laminate member 3 on the side of the incidence of light is P-type, the non-single-crystal semiconductor layer 4 on the side of the substrate 1 is N-type and the non-single-crystal semiconductor layer 5 has introduced thereinto a P-type impurity (boron) which is distributed so that the impurity concentration continuously decreases towards the non-single-crystal semiconductor layer 4 in the thickness direction of the layer 5, the same excellent operation and effects as described previously can be obtained, as will be understood from the foregoing description. In this case, however, the conductive layer 7 must be substituted with a light-transparent one. The substrate 1 and the conductive layer 2 need not be light-transparent.

While in the foregoing the non-single-crystal semiconductor laminate member 3 has one PIN junction, it is also possible to make the laminate member 3 have two or more PIN junctions and to form each of the two or more I-type non-single-crystal semiconductor layers so that the P-type impurity introduced therein may have the aforesaid concentration distribution.

It will be apparent that many modifications and variations may be effected without departing from the scope of the novel concepts of the present invention. 

What is claimed is:
 1. A semiconductor device comprising: a substrate; and a non-single crystalline semiconductor layer formed over said substrate, said semiconductor layer comprising amorphous silicon and including at least hydrogen; and at least one intrinsic or substantially intrinsic region formed within said semiconductor layer; at least one N-type or P-type region formed within said semiconductor layer; and at least one NI or PI junction between said intrinsic or substantially intrinsic region and said N-type or P-type region, wherein carbon is present in said intrinsic or substantially intrinsic region and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 2. The semiconductor device of claim 1 wherein said concentration of said carbon is not lower than 4×10¹⁵ atoms/cm³.
 3. A semiconductor device according to claim 1 wherein said intrinsic or substantially intrinsic region is formed by a chemical vapor deposition.
 4. A semiconductor device comprising: a substrate; and a non-single crystalline semiconductor layer formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and at least one intrinsic or substantially intrinsic region formed within said semiconductor layer; at least one N-type or P-type region formed within said semiconductor; and at least one NI or PI junction between said intrinsic or substantially intrinsic region and said N-type or P-type region, wherein carbon is present in said intrinsic or substantially intrinsic region and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 5. The semiconductor device of claims 1 or 4, wherein a concentration of boron in said intrinsic or substantially intrinsic region is not higher than 2×10¹⁷ atoms/cm³.
 6. The semiconductor device of claims 1 or 4, wherein a concentration of phosphor us in said N-type region is higher than 1×10¹⁹ atoms/cm³.
 7. The semiconductor device of claims 1 or 4 wherein said N-type region comprises microcrystalline silicon.
 8. The semiconductor device of claims 1 or 4, wherein said intrinsic or substantially intrinsic region has a thickness of 0.5 μm.
 9. A semiconductor device according to claim 4 wherein said intrinsic or substantially intrinsic region is formed by a chemical vapor deposition.
 10. A semiconductor device comprising: a substrate; and an amorphous semiconductor layer of intrinsic or substantially intrinsic conductivity type formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and at least one NI or PI junction formed with said amorphous semiconductor layer, wherein carbon is present in said semiconductor layer and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 11. The semiconductor device of claim 10, wherein a concentration of boron in said semiconductor layer is not higher than 2×10¹⁷ atoms/cm³.
 12. The semiconductor device of claim 10, further comprising an N-type semiconductor layer in contact with said amorphous semiconductor layer to form said NI junction therebetween, wherein a concentration of phosphorus in the N-type layer is higher than 1×10¹⁹ atoms/cm³.
 13. The semiconductor device of claim 10, where said semiconductor layer has a thickness of 0.5 μm.
 14. A semiconductor device comprising: a substrate; and an amorphous semiconductor layer of intrinsic or substantially intrinsic conductivity type formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and an N-type microcrystalline semiconductor layer comprising silicon in contact with said amorphous semiconductor layer to form at least one NI or PI junction, wherein carbon is present in said semiconductor layer and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 15. A semiconductor device according to claim 10 wherein said amorphous semiconductor layer is formed by a chemical vapor deposition.
 16. A non-single-crystalline semiconductor material comprising silicon having at least one junction formed between a substantially intrinsic or intrinsic semiconductor material and a one conductivity type semiconductor material, said junction being one of NI and PI junctions, said semiconductor material containing at least hydrogen and wherein carbon is present in said substantially intrinsic or intrinsic semiconductor material in an amount less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 17. A non-single crystalline semiconductor material according to claim 16 wherein said substantially intrinsic or intrinsic semiconductor material is formed by a chemical vapor deposition.
 18. An amorphous semiconductor material comprising silicon having at least one junction formed between a substantially intrinsic or intrinsic semiconductor material and a one conductivity type semiconductor material, said junction being one of NI and PI junctions, said semiconductor material containing at least hydrogen and wherein carbon is present in said substantially intrinsic or intrinsic semiconductor material in an amount less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 19. The semiconductor material of claims 16 or 18, wherein the concentration of boron contained in said substantially intrinsic or intrinsic semiconductor material is not higher than 2×10¹⁷ atoms/cm³.
 20. The semiconductor material of claims 16 or 18, further comprising an N-type semiconductor layer in contact with said amorphous semiconductor layer to form said NI junction therebetween, wherein a concentration of phosphorus in the N-type layer is higher than 1×10¹⁹ atoms/cm³.
 21. The semiconductor material of claims 16 or 18, further comprising an N-type semiconductor layer in contact with said amorphous semiconductor layer to form said NI junction therebetween, wherein the N-type layer comprises microcrystalline silicon.
 22. The semiconductor material of claims 16 or 18, wherein said substantially intrinsic or intrinsic semiconductor material has a thickness of 0.5 μm.
 23. An amorphous semiconductor material according to claim 18 wherein said substantially intrinsic or intrinsic semiconductor material is formed by a chemical vapor deposition.
 24. A semiconductor device comprising: a substrate; and a non-single crystalline semiconductor layer formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and at least one intrinsic or substantially intrinsic region formed within said semiconductor layer; at least one N-type or P-type region formed within said semiconductor layer; and at least one NI or PI junction between said intrinsic or substantially intrinsic region and said N-type or P-type region, wherein carbon is present in said intrinsic or substantially intrinsic region and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³, and at least a portion of said intrinsic or substantially intrinsic region contains boron in a concentration 1×10¹⁵ to 2×10¹⁷.
 25. A semiconductor device according to claim 24 wherein said intrinsic or substantially intrinsic region is formed by a chemical vapor deposition.
 26. A semiconductor device comprising: a substrate; and a non-single crystalline semiconductor layer of intrinsic or substantially intrinsic conductivity type formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and at least one NI or PI junction formed with said non-single crystalline semiconductor layer, wherein carbon is present in said intrinsic or substantially intrinsic region and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10⁵ atoms/cm³, and at least a portion of said intrinsic or substantially intrinsic region contains boron in a concentration 1×10¹⁵ to 2×10¹⁷.
 27. A semiconductor device according to claim 26 wherein said non-single crystalline semiconductor layer is formed by a chemical vapor deposition.
 28. A semiconductor device comprising: a substrate; and a non-single crystalline semiconductor layer formed over said substrate, said semiconductor layer comprising amorphous silicon including at least hydrogen; and at least one N-type or P-type region formed within said semiconductor layer; at least one second region formed within said semiconductor layer, said second region having a different conductivity type from said at least one N-type or P-type region; at least one junction between said N-type or P-type region and said second region, wherein carbon is present in said second region and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 29. A semiconductor device according to claim 28 wherein said second region is formed by a chemical vapor deposition.
 30. A semiconductor device comprising: a substrate; and an amorphous semiconductor layer formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and at least one junction formed with said amorphous semiconductor layer, wherein carbon is present in said semiconductor layer and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 31. A semiconductor device according to claim 30 wherein said amorphous semiconductor layer is formed by a chemical vapor deposition.
 32. A semiconductor device comprising: a substrate; and an amorphous semiconductor layer formed over said substrate, said semiconductor layer comprising silicon and including at least hydrogen; and an N-type semiconductor layer comprising silicon in contact with said amorphous semiconductor layer to form at least one junction, wherein carbon is present in said semiconductor layer and the concentration of said carbon is less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 33. A semiconductor device according to claim 32 wherein said amorphous semiconductor layer is formed by a chemical vapor deposition.
 34. An amorphous semiconductor material comprising silicon having at least one junction formed between a first semiconductor material and a second semiconductor material having a different conductivity type from said first semiconductor material, said first semiconductor material containing at least hydrogen and wherein carbon is present in said first semiconductor material in an amount less than 4×10¹⁸ atoms/cm³ and not lower than 4×10¹⁵ atoms/cm³.
 35. An amorphous semiconductor material according to claim 34 wherein said first semiconductor material is formed by a chemical vapor deposition. 